Composite material with thermoplastic toughened novolac-based epoxy resin matrix

ABSTRACT

Pre-impregnated composite material (prepreg) that can be cured/molded to form aerospace composite parts. The prepreg includes carbon reinforcing fibers and an uncured resin matrix. The resin matrix includes an epoxy component that is a combination of a hydrocarbon epoxy novolac resin and a trifunctional epoxy resin and optionally a tetrafunctional epoxy resin. The resin matrix includes polyethersulfone as a toughening agent and a thermoplastic particle component.

This application is a divisional of co-pending U.S. Ser. No. 15/622,585,filed on Jun. 14, 2017. U.S. Ser. No. 15/622,585 is acontinuation-in-part of U.S. Ser. No. 15/439,981, filed on Feb. 23,2017, now U.S. Pat. No. 10,000,615, which issued on Jun. 19, 2018. U.S.Ser. No. 15/622,585 is also a continuation-in-part of co-pending U.S.Ser. No. 15/189,994 filed on Jun. 22, 2016.

BACKGROUND OF THE INVENTION

1. Field of the Invention

The present invention relates generally to pre-impregnated compositematerial (prepreg) that is used in making high performance compositeparts that are especially well-suited for use as aerospace components.The present invention is directed to novolac-based epoxy resins that aretoughened with thermoplastic materials and used as the resin matrix insuch prepreg. More particularly, the present invention is directed toprepreg that include a thermoplastic toughened epoxy resin matrix thatis composed of novolac epoxy resin and triglycidyl aminophenol epoxyresin.

2. Description of Related Art

Composite materials are typically composed of a resin matrix andreinforcing fibers as the two primary constituents. Composite materialsare often required to perform in demanding environments, such as in thefield of aerospace where the physical limits and characteristics of thecomposite part is of critical importance.

Pre-impregnated composite material (prepreg) is used widely in themanufacture of composite parts. Prepreg is a combination that typicallyincludes uncured resin and fiber reinforcement, which is in a form thatis ready for molding and curing into the final composite part. Bypre-impregnating the fiber reinforcement with resin, the manufacturercan carefully control the amount and location of resin that isimpregnated into the fiber network and ensure that the resin isdistributed in the network as desired. It is well known that therelative amount of fibers and resin in a composite part and thedistribution of resin within the fiber network affect the structuralproperties of the part.

Prepreg is a preferred material for use in manufacturing load-bearing orprimary structural parts and particularly aerospace primary structuralparts, such as wings, fuselages, bulkheads and control surfaces. It isimportant that these parts have sufficient strength, damage toleranceand other requirements that are routinely established for such parts andstructures.

The fiber reinforcements that are commonly used in aerospace prepreg aremultidirectional woven fabrics or unidirectional tape that containsfibers extending parallel to each other. The fibers are typically in theform of a bundle of numerous individual fibers or filaments that isreferred to as a “tow”. The fibers or tows can also be chopped andrandomly oriented in the resin to form a non-woven mat. These variousfiber reinforcement configurations are combined with a carefullycontrolled amount of uncured resin. The resulting prepreg is typicallyplaced between protective layers and rolled up for storage or transportto the manufacturing facility. Combinations of carbon fibers and anepoxy resin matrix have become a popular combination for aerospaceprepreg.

Prepreg may also be in the form of short segments of choppedunidirectional tape that are randomly oriented to form a non-woven matof chopped unidirectional tape. This type of prepreg is referred to as a“quasi-isotropic chopped” prepreg. Quasi-isotropic chopped prepreg issimilar to the more traditional non-woven fiber mat prepreg, except thatshort lengths of chopped unidirectional tape (chips) are randomlyoriented in the tint rather than chopped fibers. This immaterial iscommonly used as a sheet molding compound to form parts and molds foruse in making parts.

The compressive and tensile strengths of a cured composite part arelargely dictated by the individual properties of the reinforcing fiberand matrix resin, as well as the interaction between these twocomponents. In addition, the fiber-resin volume ratio is an importantfactor. In many aerospace applications, it is desirable that thecomposite part exhibit high compression and tensile strengths. The openhole compression (OHC) test is a standard measure of the compressionstrength of a composite material. The open hole tension (OHT) test isalso a standard measure of the tensile strength of a composite material.

In many aerospace applications, it is desirable that the composite partexhibit high compression and/or tensile strength under both roomtemperature/dry conditions and hot/wet conditions. However, attempts tokeep compression and tensile strengths high often results in negativeeffects on other desirable properties, such as damage tolerance andinterlaminar fracture toughness.

Selecting higher modulus resins can be an effective way to increase thecompression strength of a composite. However, this can result in atendency to reduce damage tolerance, which is typically measured by adecrease in compressive properties, such as compression after impact(CAI) strength. Accordingly, it is can be difficult to achieve asimultaneous increase in both the compression and/or tensile strengthswithout deleteriously affecting the damage tolerance.

Multiple layers of prepreg are commonly used to form composite partsthat have a laminated structure. Delamination of such composite parts isan important failure mode. Delamination occurs when two layers debondfrom each other. Important design limiting factors include both theenergy needed to initiate a delamination and the energy needed topropagate it. The initiation and growth of a delamination is oftendetermined by examining Mode I and Mode II fracture toughness. Fracturetoughness is usually measured using composite materials that have aunidirectional fiber orientation. The interlaminar fracture toughness ofa composite material is quantified using the G1c (Double CantileverBeam) and G2c (End Notch Flex) tests. In Mode I, the pre-crackedlaminate failure is governed by peel forces and in Mode II the crack ispropagated by shear forces.

One approach to increasing interlaminar fracture toughness for partsmade from carbon fiber/epoxy resin prepreg has been to introducethermoplastic sheets as interleaves between layers of prepreg. However,this approach tends to yield stiff, tack-free materials that aredifficult to use. Another approach has been to add thermoplasticparticles to the epoxy resin so that a resin interlayer containing thethermoplastic particles is formed between the fiber layers of the finalpart. Polyamides have been used as such thermoplastic particles. It alsohas been known to include a thermoplastic toughening agent in the epoxyresin. The toughening agent, such as polyether sulfone (PES) orpolyetherimide (PEI), is dissolved in the epoxy resin before it isapplied to the carbon fibers. Thermoplastic toughened epoxy resins,which include a combination of both thermoplastic toughening particlesand a thermoplastic toughening agent, have been used in combination withcarbon fiber to make aerospace prepreg.

The epoxy resin matrix may include one or more types of epoxy resin. Itis known that various combinations of different types of epoxy resinsmay result in a wide variation in the properties of the final compositepart. The curing agent used to cure the epoxy resin matrix can alsosubstantially affect the properties of the final composite part. Whenformulating an epoxy resin for use as the resin matrix in aerospaceprepreg, it is difficult to predict if a new combination of epoxy resintypes and curatives will provide the desired combination of propertiesrequired for aerospace parts. This is especially the case when athermoplastic toughening agent and thermoplastic particles form part ofthe epoxy resin formulation. Accordingly, there is a great deal oftesting involved when one attempts to formulate new thermoplastictoughened epoxy resins in order to determine if the resin is suitablefor use as resin matrix in aerospace prepreg.

Although existing aerospace prepregs are well suited for their intendeduse in providing composite parts that are strong and damage tolerant,there still is a continuing need to provide aerospace prepreg that maybe used to make composite parts that exhibit desirable combinations ofhigh tensile and compressive strengths (OHC AND OHT) while maintaininghigh levels of damage tolerance (CAI) and interlaminar fracturetoughness (G1c and G2c).

SUMMARY OF THE INVENTION

In accordance with the present invention, pre-impregnated compositematerial (prepreg) is provided that can be molded to form compositeparts that have high levels of strength and also have high levels ofdamage tolerance and interlaminar fracture toughness.

The pre-impregnated composite materials of the present invention arecomposed of reinforcing fibers and an uncured resin matrix. The uncuredresin matrix includes a resin component made up of a novolac epoxy resinand triglycidyl aminophenol epoxy resin or a combination of triglycidylaminophenol epoxy and a tetrafunctional epoxy. The uncured resin matrixfurther includes a thermoplastic particle component, a thermoplastictoughening agent and a curing agent.

The present invention also covers methods for making the prepreg andmethods for molding the prepreg into a wide variety of composite parts.The invention also covers the composite parts that are made using theimproved prepreg.

It has been found that resins having the matrix resin formulation, asset forth above, can be used to form prepreg that can be molded to formcomposite parts that have unexpectedly high levels of interlaminarfracture toughness.

The above described and many other features and attendant advantages ofthe present invention will become better understood by reference to thefollowing detailed description when taken in conjunction with theaccompanying drawings.

BRIEF DESCRIPTION OF THE DRAWINGS

FIG. 1 is a perspective view of an aircraft, which depicts exemplaryprimary aircraft structures that can be made using composite materialsin accordance with the present invention.

FIG. 2 is a partial view of a helicopter rotor blade, which depictsexemplary primary aircraft structures that can he made using compositematerials in accordance with the present invention.

DETAILED DESCRIPTION OF THE INVENTION

Uncured epoxy resin compositions in accordance with the presentinvention may be used in a wide variety of situations where athermoplastic-toughened epoxy resin matrix is desired. Although theuncured epoxy resin composition may be used alone, the compositions aregenerally used as a matrix resin that is combined with a fibrous supportto form composite material composed of the fibrous support and the resinmatrix. The composite materials may be in the form of a prepreg,partially cured prepreg or a completely cured final part. The term“uncured”, when used herein in connection with: prepreg; the resinbefore impregnation into the fibrous support; the resin matrix that isformed when the fibrous support is impregnated with the resin; orcomposite material, is intended to cover items that may have beensubjected to some curing, but which have not been completely cured toform the final composite part or structure.

Although the uncured composite materials may be used for any intendedpurpose, they are preferably used in making parts for aerospacevehicles, such as commercial and military aircraft. For example, theuncured composite materials may be used to make non-primary (secondary)aircraft structures. However the preferred use of the uncured compositematerial is for structural applications, such as primary aircraftstructures. Primary aircraft structures or parts are those elements ofeither fixed-wing or rotary wing aircraft that undergo significantstress during flight and which are essential for the aircraft tomaintain controlled flight. The uncured composite materials may also beused for other structural applications to make load-bearing parts andstructures in general.

FIG. 1 depicts a fixed-wing aircraft at 10 that includes a number ofexemplary primary aircraft structures and parts that may be made usinguncured composite materials in accordance with the present invention.The exemplary primary parts or structures include the wing 12, fuselage14 and tail assembly 16. The wing 12 includes a number of exemplaryprimary aircraft parts, such as ailerons 18, leading edge 20, wing slats22, spoilers 24 trailing, edge 26 and trailing edge flaps 28. The tailassembly 16 also includes a number of exemplary primary parts, such asrudder 30, fin 32, horizontal stabilizer 34, elevators 36 and tail 38.FIG. 2 depicts the outer end portions of a helicopter rotor blade 40which includes a spar 42 and outer surface 44 as primary aircraftstructures. Other exemplary primary aircraft structures include wingspars, and a variety of flanges, clips and connectors that connectprimary parts together to form primary structures.

The pre-impregnated composite materials (prepreg) of the presentinvention may be used as a replacement for existing prepreg that isbeing used to form composite parts in the aerospace industry and in anyother application where high structural strength and damage tolerance isrequired. The invention involves substituting the resin formulations ofthe present invention in place of existing resins that are being used tomake prepreg. Accordingly, the resin formulations of the presentinvention are suitable for use as the matrix resin in conventionalprepreg manufacturing and curing processes.

The pre-impregnated composite materials of the present invention arecomposed of reinforcing fibers and an uncured resin matrix. Thereinforcing fibers can be any of the conventional fiber configurationsthat are used in the prepreg and composite sheet molding industry.Carbon fibers are preferred as the reinforcing fibers.

The resin used to form the resin matrix (matrix resin) includes a resincomponent that is made up of a hydrocarbon epoxy novolac resin incombination with a trifunctional epoxy resin and optionally atetrafunctional epoxy resin. The matrix resin further includes athermoplastic particle component, a thermoplastic toughening agent and acuring agent.

The hydrocarbon epoxy novolac resin preferably has a dicyclopentadienebackbone and is available commercially from Huntsman Corporation (TheWoodlands, Tex.) as TACTIX 556. This type of hydrocarbon novolac resinis referred to herein as a dicyclopentadiene novolac epoxy resin. Thechemical formula for TACTIX 556 is

TACTIX 556 is an amber to dark colored semi-solid hydrocarbon epoxynovolac resin that has an epoxy index (ISO 3001) of 4.25 to 4.65 eq/kgand epoxy equivalent (ISO 3001) of 215-235 g/eq. The Viscosity of TACTIX556 at 79° C. (ISO 9371B) is 2250 mPa·s. Dicyclopentadiene epoxy novolacresins other than TACTIX 556 may be used in place of TACTIX 556 providedthey have the same chemical formula and properties. For example, anothersuitable dicyclopentadiene epoxy novolac resin is XD-1000-2L which isavailable commercially from Nippon Kayaku Co., Ltd (Chiyoda-ku, Tokyo).TACTIX 556 is the preferred hydrocarbon epoxy novolac resin for use inaccordance with the present invention.

When a tetrafunctional epoxy resin is included in the resin component,the amount of hydrocarbon epoxy novolac resin present in the uncuredresin may vary from 8 to 20 weight percent based on the total weight ofthe uncured resin matrix. Preferably, the uncured resin will containfrom 10 to 17 weight percent dicyclopentadiene hydrocarbon epoxy novolacresin. Uncured resin formulations that contains from 13 to 15 weightpercent dicyclopentadiene hydrocarbon epoxy novolac resin areparticularly preferred because they provide an unexpectedly high G2c ofabout 13 when the ratio of polyamide particles to polyimide particles isfrom 3.2:1 to 2.8:1. In this embodiment of the invention, which isreferred to herein as the DEN/TRIF/TETF matrix resin, the uncured resincomponent is composed of dicyclopentadiene epoxy novolac resin, atrifunctional epoxy resin and a tetrafunctional epoxy resin.

In the DEN/TRIF/TETF matrix resin, a preferred exemplary trifunctionalepoxy resin is triglycidyl para-aminophenol. Triglycidylpara-aminophenol is available commercially from Huntsman AdvancedMaterials (The Woodlands, Tex.) under the trade name Araldite MY0510.Another suitable trifunctional epoxy resin is triglycidylmeta-aminophenol. Triglycidyl meta-aminophenol is available commerciallyfrom Huntsman Advanced Materials (The Woodlands, Tex.) under the tradename Araldite MY0600 and from Sumitomo Chemical Co. (Osaka, Japan) underthe trade name ELM-120. Other trifunctional epoxy resins may be usedprovided that they have properties that are the same or similar to theproperties of triglycidyl para-aminophenol or triglycidylmeta-aminophenol.

In the DEN/TRIF/TETF matrix resin embodiment, an exemplarytetrafunctional epoxy resin isN,N,N′,N′-tetraglycidyl-4,4′-diaminodiphenyl methane (TGDDM) which isavailable commercially as Araldite MY720 and MY721 from HuntsmanAdvanced Materials (The Woodlands, Tex.), or ELM 434 from SumitomoChemical Industries, Ltd. (Gleno, Tokyo). Other tetrafunctional epoxyresins may be used provided that they have properties that are the sameor similar to the properties ofN,N,N′,N′-tetraglycidyl-4,4′-diaminodiphenyl methane.

In the DEN/TRIF/TETF matrix resin, the total amount of trifunctional andtetrafunctional epoxy resin may vary from 35 to 45 weight percent basedon the total weight of the uncured resin. It is preferred that that theweight ratio between the trifunctional and tetrafunctional resins befrom 1.0:1.5 to 1.5:1.0. It is particularly preferred that the weightratio between the trifunctional and tetrafunctional resins be from1.1:1.0 to 1.3:1.0.

In another embodiment of the invention, the resin component containsonly dicyclopentadiene novolac epoxy resin and triglycidyl aminophenolepoxy resin. In the resin component of this embodiment, which isreferred to herein as the DEN/TRIF matrix resin, the dicyclopentadienenovolac epoxy resin is present in the range 4 wt % to 30 wt %, based onthe total weight of the uncured resin matrix. Preferably, thedicyclopentadiene novolac epoxy resin is present in the range 17 wt % to27 wt %, based on the total weight of the uncured resin matrix. Morepreferably, the dicyclopentadiene novolac epoxy resin is present in therange 20 wt % to 24 wt %, based on the total weight of the uncured resinmatrix.

In the DEN/TRIF matrix resin, the triglycidyl aminophenol epoxy resin ispresent in the range 20 wt % to 55 wt %, based on the total weight ofthe uncured resin matrix. Preferably, the triglycidyl aminophenol epoxyresin is present in the range 26 wt % to 36 wt %, based on the totalweight of the uncured resin matrix. More preferably, the triglycidylaminophenol epoxy resin is present in the range 29 wt % to 33 wt %,based on the total weight of the uncured resin matrix. Triglycidylmeta-aminophenol is the preferred type of triglycidyl aminophenol epoxyresin for the DEN/TRIF matrix resin.

In the DEN/TRIF matrix resin, the weight ratio of triglycidylaminophenol epoxy resin to dicyclopentadiene novolac epoxy resin mayvary from 1:1 to 10.511. The preferred weight ratio range of triglycidylaminophenol epoxy resin to dicyclopentadiene novolac epoxy resin is from1.2:1 to 1.6:1. Most preferred is a weight ratio of triglycidylaminophenol epoxy resin to dicyclopentadiene novolac epoxy resin that isabout 1.4:1.

The uncured resin matrix in accordance with the present invention alsoincludes a thermoplastic particle component that contains one or moretypes of thermoplastic particles. Exemplary thermoplastic particles arepolyamide particles which are formed from the polymeric condensationproduct of a methyl derivative of bis(4-aminocyclohexyl)methane and analiphatic dicarboxylic acid selected from the group consisting of decanedicarboxylic acid and dodecane dicarboxylic acid. Methyl derivatives ofbis(4-aminocyclohexyl)methane, which are referred to herein as the“amine component” are also known as methyl derivatives of4,4′-diaminocyclohexylmethane. This type of polyamide particle and themethods for making them are described in detail in U.S. Pat. Nos.3,936,426 and 5,696,202, the contents of which are hereby incorporatedby reference.

The formula for the amine component of the polymeric condensationproduct is

-   -   where R₂ is hydrogen and R₁ is either methyl or hydrogen.

The formula for the monomeric unit of the polymeric condensation productmay be represented as follows:

The molecular number of the polymeric condensation product will rangefrom 14,000 to 20,000 with a molecular numbers of about 17000 beingpreferred.

The polyamide particles should have particle sizes of below 100 microns.It is preferred that the particles range in size from 5 to 60 micronsand more preferably from 10 to 30 microns. It is preferred that theaverage particle size is from 15 to 25 microns. The polyamide particlesmay be regular or irregular in shape. For example, the particles may besubstantially spherical or they can be particles with a jagged shape.

One exemplary polyamide particle is made from polyamide where the aminecomponent of the polymeric condensation product has the above formula inwhich R₁ both are methyl and R₂ both are hydrogen. Such polyamideparticles may be made from the polymeric condensation product of3,3′-dimethyl-bis(4-aminocyclohexyl)-methane and 1,10-decanedicarboxylic acid. The polyamide particles are made by combining, in aheated receiving vessel, 13,800 grams of 1,10-decane dicarboxylic acidand 12,870 grams of 3,3′-dimethyl-bis(4-aminocyclohexy)methane with 30grams of 50% aqueous phosphoric acid, 150 grams benzoic acid and 101grams of water. The mixture is stirred in a pressure autoclave untilhomogeneous. After a compression, decompression and degassing phase, thepolyamide condensation product is pressed out as a strand, passed undercold water and granulated to form the polyamide particles. Polyamideparticles where R₁ both are methyl and R₂ both are hydrogen can also bemade from GRILAMID TR90, which is commercially available from EMS-Chime(Sumter, S.C.). GRILAMID TR90 is the polymeric condensation product of3,3)-dimethyl-bis(4-aminocyclohexyl)-methane and 1,10-decanedicarboxylic acid.

Another exemplary polyamide particle is made from polyamide here theamine component of the polymeric condensation product has the aboveformula in which R₁ both are methyl and R₂ both are methyl. Suchpolyamide particles may be made in the same manner as described above,except that polyamide is the polymeric condensation product of3,3′-dimethyl-bis(4-aminocyclohexyl)-propane and 1,10-decanedicarboxylic acid. Polyamide particles where R₁ both are methyl and R₂both are methyl can also be made from CX7323, which is commerciallyavailable from Evonik (Mobile, Ala.). CX7323 is the polymericcondensation product of 3,3′-dimethyl-bis(4-aminocyclohexyl)-propane and1,10-decane dicarboxylic acid. Mixtures of these two exemplary polyamideparticles may be used, if desired.

The thermoplastic particle component may include one or more types ofpolyamide particles that are typically used in thermoplastic toughenedepoxy resins including, for example, polyamide (PA) 11, PA6, PA12,PA6/PA12 copolymer, PA4, PA8, PA6.6, PA4.6, PA10.10, PA6.10 and PA10.12.

A preferred thermoplastic particle component contains a first group ofpolyamide particles which do not contain crosslinked polyamide a secondgroup of polyamide particles that do contain crosslinked polyamide.

The first group of polyamide particles may be any of the polyamideparticle that do not contain crosslinked polyamide and which aretypically used in thermoplastic toughened epoxy-based prepreg. Suchparticles may be composed of polyamide (PA) 11, PA6, PA12, PA6/PA12copolymer, PA4, PA8, PA6.6, PA4.6, PA10.10, PA6.10 and PA10.12.Non-crosslinked polyamide particles are available commercially from anumber of sources. Suitable non-crosslinked polyamide 12 particles areavailable from Kobo Products under the trade name SP10L. SP10L particlescontain over 98 wt % PA 12. The particle size distribution is from 7microns to 13 microns with the average particle size being 10 microns.The density of the particles is 1 gm³. It is preferred that the PA12particles are at least 95 wt % PA12, excluding moisture content.

Other suitable non-crosslinked particles are available from Arkema(Colombes, France) under the tradenames Orgasol 1002 powder and Orgasol3803 powder. Orgasol 1002 powder is composed of 100% PA6 particleshaving an average particle size of 20 microns. Orgasol 3803 is composedof particles that are a copolymer of 80% PA12 and 20% PA6 with the meanparticle size being from 17 to 24 microns. Orgasol 2002 is a powdercomposed of non-crosslinked PA12 particles that may also be used in thefirst group of particles.

The preferred non-crosslinked polyamide particles for the first group ofthermoplastic particles are polyamide 11 particles, which are alsoavailable commercially from a number of sources. The preferred polyamide11 particles are available from Arkema (Colombes, France) under thetrade name Rislan PA11. These particles contain over 98 wt % PA 11 andhave a particle size distribution of 15 microns to 25 microns. Theaverage particle size is 20 microns. The density of the Rislan PA11particles is 1 g/cm³. It is preferred that the PA 11 particles are atleast 95 wt % PA11, excluding moisture content.

The second group of thermoplastic polyamide particles are particles thatcontain crosslinked polyamide on the surface of the particle, in theinterior of the particle or both. The crosslinked polyamide particlesmay be made from polyamide that has been crosslinked prior to particleformation or non-crosslinked polyamide particles may be treated withsuitable crosslinking agents to produce crosslinked polyamide particles.

Suitable crosslinked particles contain crosslinked PA11, PA6, PA12,PA6/PA12 copolymer, PA4, PA8, PA6.6, PA4.6, PA10.10, PA6.10 and PA10.12.Any of the crosslinking agents commonly used to cross link polyamide aresuitable. Exemplary crosslinking agents are epoxy-based crosslinkingagents, isocyanate-based crosslinking agents, carbodiimide-basedcrosslinking agents, acyllactam-based crosslinking agents andoxazoline-based crosslinking agent. Preferred crosslinked particles arePA12 particles that contain PA12 that has been crosslinked with an epoxycrosslinking agent. The procedures used to cross link thermoplasticpolymers, including polyamide, are known. For examples, see U.S. Pat.No. 6,399,714, U.S. Pat. No. 8,846,818 and U.S. Published PatentApplication US 2016/0152782 A1. The contents of these three referencesare hereby incorporated by reference.

Crosslinked PA12 particles are available commercially from Arkema(Colombes, France) under the tradename ORGASOL 2009 polyamide powder,which is also known as CG352. The PA12 particles present in ORGASOL 2009polyamide powder are composed of at least 40% PA12 that has been crosslinked with an epoxy-based crosslinking agent. The ORGASOL 2009crosslinked polyamide particles have an average particle size of 14.2microns with only 0.2% of the particles having a diameter of greaterthan 30 microns. The melting point of ORGASOL 2009 crosslinked particlesis 180° C. The specific surface area of the ORGASOL 2009 particles is1.9 and the moisture content of the particles is 0.34%.

The crosslinked polyamide particles should each contain from 40 to 70%crosslinked polyamide. Preferably, the crosslinked polyamide particlesshould each contain from 40 to 60% crosslinked polyamide.

Preferably, both the non-crosslinked and crosslinked polyamide particlesshould have particle sizes of below 100 microns. It is preferred thatthe particles range in size from 5 to 60 microns and more preferablyfrom 5 to 30 microns. It is preferred that the average particle size isfrom 5 to 20 microns. The particles may be regular or irregular inshape. For example, the particles may be substantially spherical or theycan be particles with a jagged shape. It is preferred that thenon-crosslinked particles have an average particle size that is largerthan the crosslinked particles. Preferably, the average non-crosslinkedparticles size will range from 15 to 25 microns and the averagecrosslinked particle size will range from 10 to 20 microns.

The thermoplastic particle component is present in the range 5 wt % to20 wt %, based on the total weight of the uncured resin matrix.Preferably, there will be from 7 to 17 wt % thermoplastic particlecomponent. The relative amounts of non-crosslinked and crosslinkedparticles may be varied when a combination of crosslinked andnon-crosslinked particles are used. Weight ratios of non-crosslinkedparticles to crosslinked particles may range from 4:1 to 1.5:1.Preferably, the weight ratios of non-crosslinked particles tocrosslinked particles will range from 3.5:1 to 2.5:1. A combination ofnon-crosslinked and crosslinked particles is a preferred thermoplasticparticle component for use with the DEN/TRIF matrix resin embodiment.

In the DEN/TRIF matrix resin embodiment, the total amount of polyamideparticles in the uncured resin may vary from 9 to 21 weight percentbased on the total weight of the uncured resin. Preferably, the totalamount of polyamide particles in the uncured resin will range from 11 wt% to 19 wt % based on the total weight of the uncured resin matrix. Morepreferably, the total amount of polyamide particles in the uncured resinwill range from 12 wt % to 17 wt %, based on the total weight of theuncured resin matrix.

The thermoplastic particle component may include a combination ofpolyimide particles and polyamide particles where the polyamideparticles are composed of the polymeric condensation product of a methylderivative of bis(4-aminocyclohexyl)methane and an aliphaticdicarboxylic acid. This particle combination is a preferredthermoplastic particle component for use with the DEN/TRIF/TETF matrixresin embodiment.

Preferred polyimide particles are available commercially from HP PolymerGmbH (Lenzig, Austria) as P84 polyimide molding powder. Suitablepolyamide particles are also available commercially from EvonikIndustries (Austria) under the tradename P84NT. The polyimide used tomake the particles is disclosed in U.S. Pat No. 3,708,458, the contentsof which is hereby incorporated by reference. The polyimide is, made bycombining benzophenone-3,3′,4,4′-tetracarboxylic acid dianhydride with amixture of 4,4′-methylenebis(phenyl isocyanate) and toluene diisocyanate(2,4- or 2,6-isomer). The amine analogs may be used in place of thearomatic iso- and diisocyanates. The CAS Registry No. of the polyimideis 58698-66-1.

The polyimide particles are composed of an aromatic polyimide having therepeating monomer formula:

where from 10 to 90% of the R groups in the overall polymer are anaromatic group having the formula:

with the remaining R groups in the polymer being

The size of the polyimide particles in the powder typically ranges from2 microns to 35 microns. A preferred polyimide powder will containparticles that range in size from 2 to 30 microns with the averageparticle size ranging from 5 microns to 15 microns. Preferably, at least90 weight percent of the polyimide particles in the powder will be inthe size range of 2 microns to 20 microns. The polyimide particles maybe regular or irregular in shape. For example, the particles may besubstantially spherical or they can be particles with a jagged shape.

The polyimide particles contain at least 95 weight percent polyimide.Small amounts (up to 5 weight percent) of other materials may beincluded in the particles provided that they do not adversely affect theoverall characteristics of the particles.

The glass transition temperature (Tg) of the polyimide particles shouldbe about 330° C. with the density of individual particles being 1.34grams per cubic centimeter. The linear coefficient of thermal expansionof the particles is 50.

The total amount of thermoplastic particles in the uncured DEN/TRIF/TETFmatrix resin embodiment is preferably from 9 to 15 weight percent basedon the total weight of the uncured resin. In order to obtain highresistance to delamination, the weight ratio between the polyamideparticles and the polyimide particles can range from 3.5:1.0 to 1.0:1.0.Preferably, the weight ratio between the polyamide particles andpolyimide particles is between 3.2:1.0 and 2.8:1.0. In a particularlypreferred DEN/TRIF/TETF matrix resin, the amount of polyamide particlesis from 8 to 10 weight percent of the total weight of the uncured resinand the amount of polyimide particles is from 2 to 4 weight percent ofthe total weight of the uncured resin.

The uncured resin matrix includes at least one curing agent. Suitablecuring agents are those which facilitate the curing of theepoxy-functional compounds of the invention and, particularly,facilitate the ring opening polymerization of such epoxy compounds. In aparticularly preferred embodiment, such curing agents include thosecompounds which polymerize with the epoxy-functional compound orcompounds, in the ring opening polymerization thereof. Two or more suchcuring agents may be used in combination.

Suitable curing agents include anhydrides, particularly polycarboxylicanhydrides, such as nadic anhydride (NA), methylnadic anhydride(MNA—available from Aldrich), phthalic anhydride, tetrahydrophthalicanhydride, hexahydrophthalic anhydride (HHPA—available from Anhydridesand Chemicals Inc., Newark, N.J.), methyltetrahydrophthalic anhydride(MTHPA—available from Anhydrides and Chemicals Inc.),methylhexahydrophthalic anhydride (MHHPA—available from Anhydrides andChemicals Inc.), endomethylenetetrahydrophthalic anhydride,hexachloroendomethylenetetrahydrophthalic anhydride (ChlorenticAnhydride—available from Velsicol Chemical Corporation, Rosemont, Ill.),trimellitic anhydride, pyromellitic dianhydride, maleic anhydride(MA—available from Aldrich), succinic anhydride (SA), nonenylsuccinicanhydride, dodecenylsuccinic anhydride (DDSA—available from Anhydridesand Chemicals Inc.), polysebacic polyanhydride, and polyazelaicpolyanhydride.

Further suitable curing agents are the amines, including aromaticamities, e.g., 1,3-diaminobenzene, 1,4-diaminobenzene,4,4′-diamino-diphenylmethane and the polyaminosulphones, such as4,4′-diaminodiphenyl sulphone (4,4′-DDS—available from Huntsman),4-aminophenyl sulphone, and 3,3′- diaminodiphenyl sulphone (3,3′-DDS).Also, suitable curing agents may include polyols, such as ethyleneglycol (EG—available from Aldrich), polypropylene glycol), andpoly(vinyl alcohol); and the phenol-formaldehyde resins, such as thephenol-formaldehyde resin having an average molecular weight of about550-650, the p-t-butylphenol-formaldehyde resin having an averagemolecular weight of about 600-700, and the p-n-octylphenol-formaldehyderesin, having an average molecular weight of about 1200-1400, thesebeing available as HRJ 2210, HRJ-2255, and SP-1068, respectively fromSchenectady Chemicals, Inc., Schenectady, N.Y.). Further as tophenol-formaldehyde resins, a combination of CTU guanamine, andphenol-formaldehyde resin having a molecular weight of 398, which iscommercially available as CG-125 from Ajinomoto USA Inc. (Teaneck,N.J.),. is also suitable.

Different commercially available compositions may be used as curingagents in the present invention. One such composition is AH-154, adicyandiamide type formulation available from Ajinomoto USA Inc. Otherswhich are suitable include Ancamide 400, which is a mixture ofpolyamide, diethyltriamine, and triethylenetetraamine, Ancamide 506,which is a mixture of amidoamine, imidazoline, andtetraethylenepentaamine, and Ancamide 1284, which is a mixture of4,4′-methylenedianiline and 1,3-benzenediamine; these formulations areavailable from Pacific Anchor Chemical, Performance Chemical Division,Air Products and Chemicals, Inc., Allentown, Pa.

Additional suitable curing agents include imidazole(1,3-diaza-2,4-cyclopentadiene) available from Sigma Aldrich (St. Louis,Mo.), 2-ethyl-4-methylimidazole available from Sigma Aldrich, and borontrifluoride amine complexes, such as Anchor 1170, available from AirProducts & Chemicals, Inc.

Still additional suitable curing agents include3,9-bis(3-aminopropyl-2,4,8,10-tetroxaspiro[5.5]undecane, which iscommercially available as ATU, from Ajinomoto USA Inc., as well asaliphatic dihydrazide, which is commercially available as Ajicure UDH,also from Ajinomoto USA Inc., and mercapto-terminated polysulphide,which is commercially available as LP540, from Morton International,Inc. Chicago. Ill.

The curing agent(s) is selected so that it provides curing of the matrixat suitable temperatures. The amount of curing agent required to provideadequate curing of the matrix will vary depending upon a number offactors including the type of resin being cured, the desired curingtemperature and curing time. Curing agents typically may also includecyanoguanidine aromatic and aliphatic amines, acid anhydrides, LewisAcids, substituted ureas, imidazoles and hydrazines. The particularamount of curing agent required for each particular situation may bedetermined by well-established routine experimentation.

Exemplary preferred curing agents include 4,4′-diaminodiphenyl sulphone(4,4′-DDS) and 3,3′-dianthiodiphenyl sulphone (3,3′-DDS), bothcommercially available from Huntsman.

The curing agent is present in an amount that ranges from 10 wt % to 30wt % of the uncured resin matrix. In the DEN/TRIF matrix resin, thecuring agent is present in an amount that ranges from 17 wt % to 27 wt%. More preferably, the curing agent is present in the range 21 wt % to25 wt % of the uncured resin matrix. In the DEN/TRIF matrix resin,4,4′-DDS is a preferred curing agent. It is preferably used as the solecuring agent in an amount ranging from 20 wt % to 26 wt %. Small amounts(less than 5 wt %) of other curatives, such as 3,3′-DDS, may beincluded, if desired.

In the DEN/TRIF/TETF matrix resin, the curing agent is present in anamount that ranges from 15 wt % to 30 wt % of the uncured resin.Preferably, the curing agent is present in an amount that ranges from 20wt % to 30 wt %. 3,3′-DDS is the preferred curing agent. It preferablyused as the sole curing agent in amounts ranging from 24 to 28 weightpercent based on the total weight of the uncured resin. Small amounts(less than 5 wt %) of other curatives, such as 4,4′-DDS, may beincluded, if desired.

Accelerators may also being included to enhance or promote curing.Suitable accelerators are any of the crone compounds that have beencommonly used in the curing of epoxy resins. Specific examples ofaccelerators, which may be used alone or in combination, includeN,N-dimethyl, N′-3,4-dichlorphenyl urea (Diuron), N′-3-chlorophenyl urea(Monuron), and preferably N,N-(4-methyl-m-phenylenebis[N′,N′-dimethylurea] (e.g. Dyhard UR500 available from Degussa).

The uncured resin matrix of the present invention also includes athermoplastic toughening agent. Any suitable thermoplastic polymers maybe used as the toughening agent. Typically, the thermoplastic polymer isadded to the resin mix as particles that are dissolved in the resinmixture by heating prior to addition of the curing agent. Once thethermoplastic agent is substantially dissolved in the hot matrix resinprecursor (i.e. the blend of epoxy resins), the precursor is cooled andthe remaining ingredients (curing agent and insoluble thermoplasticparticles) are added and mixed with the cooled resin blend.

Exemplary thermoplastic toughening agents/particles include any of thefollowing thermoplastics, either alone or in combination: polysulfone,polyethersulfone, polyetherimide, high performance hydrocarbon polymers,elastomers, and segmented elastomers.

A suitable toughening agent, by way of example, is particulatepolyethersulfone (PES) that is sold under the trade name Sumikaexcel5003P, and which is commercially available from Sumitomo Chemicals (NewYork, N.Y.). Alternatives to 5003P are Solvay polyethersulphone 105RP,or the non-hydroxyl terminated grades such as Solvay 1054P which iscommercially available from Solvay Chemicals (Houston, Tex.). DensifiedPES particles may be used as the toughening agent. The form of the PESis not particularly important since the PES is dissolved duringformation of the resin. Densified PES particles can be made inaccordance with the teachings of U.S. Pat. No. 4,945,154, the contentsof which are hereby incorporated by reference. Densified PES particlesare also available commercially from Hexcel Corporation (Dublin, Calif.)under the trade name HRI-1. The average particle size of the tougheningagent should be less than 100 microns to promote and insure completedissolution of the PES in the matrix.

In the DEN/TRIF matrix resin, the toughening agent is present in therange 5 wt % to 15 wt %, based on the total weight of the uncured resinmatrix. Preferably, the toughening agent is present in the range 7 wt to12 wt %. More preferably, the toughening agent is present in the range 8wt % to l 1 wt %.

In the DEN/TRIF/TETF matrix resin, the PES toughening agent is presentin the range 5 wt % to 26 wt %, based on the total weight of the uncuredresin. Preferably, the toughening agent is present in the range 7 wt %to 14 wt %. The preferred amount of PES for use in making resins withrelatively low minimum viscosity (25-45 Poise) is from 7 to 9 weightpercent based on the total weight of the uncured resin. The preferredamount of PES for use in making resins with relatively high minimumviscosity (55-75 Poise) is from 10 to 13 weight percent based on thetotal weight of the uncured resin.

The matrix resin may also include additional ingredients, such asperformance enhancing or modifying agents provided they do not adverselyaffect the tack and out-life of the prepreg or the strength and damagetolerance of the cured composite part. The performance enhancing ormodifying agents, for example, may be selected from core shell rubbers,flame retardants, wetting agents, pigments/dyes, UV absorbers,anti-fungal compounds, fillers, conducting particles, and viscositymodifiers.

Exemplary core shell rubber (CSR) particles are composed of across-linked rubber core, typically a copolymer of butadiene, and ashell composed of styrene, methyl methacrylate, glycidyl methacrylateand/or acrylonitrile. The core shell particles are usually provided asparticles dispersed in an epoxy resin. The size range of the particlesis typically from 50 to 150 nm. Suitable CSR particles are described indetail in U.S. Patent Publication US2007/0027233A1, the contents ofwhich is hereby incorporated by reference. Preferred core shellparticles are MX core-shell particles, which are available from Kane Ace(Pasadena, Tex.). A preferred core shell particle for inclusion in theDEN/TRIF matrix resin is Kane Ace MX-418. MX-418 is supplied as a 25 wt% suspension of core shell particles in a tetrafunctional epoxy resin.The core shell particles in MX-418 are polybutadiene (PBd) core shellparticles which have an average particle size of 100 nanometers.

Suitable fillers include, by way of example, any of the following eitheralone or in combination: silica, alumina, titania, glass, calciumcarbonate and calcium oxide.

Suitable conducting particles, by way of example, include any of thefollowing either alone or in combination: silver, gold, copper,aluminum, nickel, conducting grades of carbon, buckminsterfullerene,carbon nanotubes and carbon nanofibres. Metal-coated fillers may also beused, for example nickel coated carbon particles and silver coatedcopper particles.

Potato shaped graphite (PSG) particles are suitable conductingparticles. The use of PSG particles in carbon fiberlepoxy resincomposites is described in detail in U.S. Patent Publication No. US2015/0179298 A1, the contents of which is hereby incorporated byreference. The PSG particles are commercially available from NGSNaturgraphit (Germany) as SG25/99.95 SC particles or from Nippon PowerGraphite Company (Japan) as GHDR-15-4 particles. These commerciallyavailable PSG particles have average particle sizes of from 10-30microns with the GHDR-15-4 particles having a vapor deposited coating ofcarbon on the outer surface of the PSG particles.

The uncured resin matrix may include small amounts (less than 5 wt % andpreferably less than 1 wt %) of an additional epoxy or non-epoxythermosetting polymeric resin. For DEN/TRIF/TETF matrix resins, theepoxy resin component contains at least 95 wt % DEN, TRIF and TETF andmore preferably at least 99 wt % of the three epoxy resins. For DEN/TRIFmatrix resins, the epoxy resin component contains at least 95 wt % DENand TRIF and more preferably at least 99 wt % of the two epoxy resins.Suitable additional epoxy resins include difunctional epoxy resins, suchas bisphenol A and bisphenol F type epoxy resins. Suitable non-epoxythermoset resin materials for the present invention include, but are notlimited to, resins of phenol formaldehyde, urea-formaldehyde,1,3,5-triazine-2,4,6-triamine (Melamine) bismaleimide, vinyl esterresins. benzoxazine resins, phenolic resins, polyesters, cyanate esterresins or any combination thereof. The additional thermoset resin, ifany, is preferably selected from epoxy resins, cyanate ester resins,benzoxazine and phenolic resins.

The uncured resin is made in accordance with standard prepreg matrixresin processing. In general, the hydrocarbon novolac epoxy resin andother epoxy resin(s) are mixed together at room temperature to form aresin mix to which the thermoplastic toughening agent is added. Thismixture is then heated to about 120° C. for about 1 to 2 hours todissolve the thermoplastic toughening agent. The mixture is then cooleddown to about 80° C. and the remainder of the ingredients (thermoplasticparticle component, curing agent and other additive, if any) is mixedinto the resin to form the final uncured resin matrix that isimpregnated into the fiber reinforcement.

The uncured resin is applied to the fibrous reinforcement to form anuncured resin matrix in accordance with any of the known prepregmanufacturing techniques. The fibrous reinforcement may be fully orpartially impregnated with the uncured resin. In an alternateembodiment, the uncured resin may be applied to the fiber fibrousreinforcement as a separate layer, which is proximal to, and in contactwith, the fibrous reinforcement, but does not substantially impregnatethe fibrous reinforcement. The prepreg, which is also referred to assemi-preg, is typically covered on both sides with a protective film androlled up for storage and shipment at temperatures that are typicallykept well below room temperature to avoid premature curing. The actualresin matrix is not formed until further processing of the semi-preg.Any of the other prepreg manufacturing processes and storage/shippingsystems may be used if desired.

The fibrous reinforcement of the prepreg may be selected from anyfiberglass, carbon or aramid (aromatic polyamide) fibers. The fibrousreinforcement is preferably carbon fibers. Preferred carbon fibers arein the form of tows that contain from 3,000 to 50,000 carbon filaments(3K to 50K). Commercially available carbon fiber tows that contain 6,000or 24,000 carbon filaments (6K or 24K) are preferred.

The uncured matrix resins of the present invention are particularlyeffective in providing laminates that have high strength properties anddamage tolerance when the carbon tow contains from 6,000 to 24,000filaments, the tensile strength is from 750 to 860 ksi, the tensilemodulus is from 35 to 45 Msi, the strain at failure is 1.5 to 2.5%, thedensity is 1.6 to 2.0 g/cm³ and the weight per length is from 0.2 to 0.6g/m. 6K and 12K IM7 carbon tows (available from Hexcel Corporation) arepreferred. IM7 12K fibers have a tensile strength of 820 ksi, thetensile modulus is 40 Msi, the strain at failure is 1.9%, the density is1.78 g/cm³ and the weight per length is 0.45 g/m. IM7 6K fibers have atensile strength of 800 ksi, the tensile modulus is 40 Msi, the strainat failure is 1.9%, the density is 1.78 g/cm³ and the weight per lengthis 0.22 g/m. IM7 fibers and carbon fibers with similar properties aregenerally considered to be intermediate modulus carbon fibers. IM8carbon fibers, which are commercially available from Hexcel Corporation(Dublin, Calif.) are also a preferred type of medium modulus carbonfiber.

The fibrous reinforcement may comprise cracked (i.e. stretch-broken) orselectively discontinuous fibers, or continuous fibers. The use ofcracked or selectively discontinuous fibers may facilitate lay-up of thecomposite material prior to being hilly cured, and improve itscapability of being shaped. The fibrous reinforcement may be in a woven,non-crimped, non-woven, unidirectional, or multi-axial textile structureform, such as quasi-isotropic chopped prepreg that is used to form sheetmolding compound. The woven form may be selected from a plain, satin, ortwill weave style. The non-crimped and multi-axial forms may have anumber of plies and fiber orientations. Such styles and forms are wellknown in the composite reinforcement field, and are commerciallyavailable from a number of companies, including Hexcel Reinforcements(Les Avenieres, France).

The prepreg may be in the form of continuous tapes, towpregs, webs, orchopped lengths (chopping and slitting operations may be carried out atany point after impregnation). The prepreg may be an adhesive orsurfacing film and may additionally have embedded carriers in variousforms both woven, knitted, and non-woven. The prepreg may be fully oronly partially impregnated, for example, to facilitate air removalduring curing.

The following exemplary DEN/TRIF/TETF resin formulations may beimpregnated into a fibrous support to form a resin matrix in accordancewith the present invention (all weight percentages are based on thetotal resin weight):

-   1) 9 wt % to 11 wt % dicyclopentadiene novolac epoxy resin    (TACTIX®556); 21 wt % to 23 wt % triglycidyl-p-aminophenol (MY0510);    17 wt % to 19 wt % tetrafunctional epoxy (MY721); 10 wt % to 13 wt %    polyethersulfone (5003P): 8 wt % to 10 wt % polyimide particles    (P84HCM), 2 wt % to 4 wt % particles made from the condensation    product of 3,3′-dimethyl-bis(4-aminocyclohexyl)-methane and    1,10-decane dicarboxylic acid (GRILAMID TR90); and 25 wt % to 28 wt    % 3,3′-DDS as the curing agent.-   2) 13 wt % to 16 wt % dicyclopentadiene novolac epoxy resin    (TACTIX®556); 18 wt % to 20 wt triglycidyl-p-aminophenol (MY0510);    17 wt % to 19 wt % tetrafunctional epoxy (MY721); 10 wt % to 13 wt %    polyethersulfone (5003P); 8 wt % to 10 wt % polyimide particles    (P84HCM); 2 wt % to 4 wt % particles made from the condensation    product of 3,3′-dimethyl-bis(4-aminocyclohexyl)-methane and    1,10-decane dicarboxylic acid (GRILAMID TR90); and 25 wt % to 28 wt    % 3,3′-DDS as the curing agent.-   3) 16 wt % to 18 wt % dicyclopentadiene novolac epoxy resin    (TACTIX®556); 14 wt % to 16 wt % triglycidyl-p-aminophenol (MY0510):    17 wt % to 19 wt % tetrafunctional epoxy (MY721); 10 wt % to 13 wt %    polyethersulfone (5003P); 5 wt % to 7 wt % polyimide particles    (P84HCM); 5 wt % to 7 wt % particles made from the condensation    product of 3,3′-dimethyl-bis(4-aminocyclohexyl)-methane and    1,10-decane dicarboxylic acid (GRILAMID TR90); and 25 wt % to 28 wt    % 3,3′-DDS as the curing agent.-   4) 13 wt % to 16 wt % dicyclopentadiene novolac epoxy resin    (TACTIX®556); 19 wt % to 21 wt % triglycidyl-p-aminophenol (MY0510);    18 wt % to 20 wt % tetra functional epoxy Ny721); 7 wt % to 9 wt %    polyethersulfone (5003P); 2 wt % to 4 wt % polyimide particles    (P84HCM); 8 wt % to 10 wt % particles made from the condensation    product of 3,3′-dimethyl-bis(4-aminocyclohexyl)-methane and    1,10-decane dicarboxylic acid (GRILAMID TR90); and 25 wt % to 28 wt    % 3,3′-DDS as the curing agent.-   5) 9 to 11 wt % dicyclopentadiene novolac epoxy resin (TACTIX®556);    21 wt % to 23 wt % triglycidyl-p-aminophenol (MY0510); 19 wt % to 22    wt % tetrafunctional epoxy (MY721); 7 wt % to 9 wt %    polyethersulfone (5003P); 2 wt % to 4 wt % polyimide particles    (P84HCM): 8 wt % to 10 wt % particles made from the condensation    product of 3,3′-dimethyl-bis(4-aminocyclohexyl)-methane and    1,10-decane dicarboxylic acid (GRILAMID TR90); and 26 wt % to 29 wt    % 3,3′-DDS as the curing agent.

With respect to the DEN/TRIF matrix resin embodiments of the invention,a preferred exemplary DEN/TRIF matrix resin includes from 29 wt % to 33wt % triglycidyl-m-aminophenol (MY0600); from 20 wt % to 24 wt %hydrocarbon novolac epoxy resin (TACTIX 556); from 7 wt % to 11 wt %polyethersulfone (5003P) as a toughening agent; from 2 wt % to 7 wt %crosslinked polyamide 12 particles (ORGASOL 2009); from 9 wt % to 13 wt% polyamide 11 particles (Rislan PA11) where the weight ratio ofpolyamide 11 particles to crosslinked polyamide 12 particles is from2.5:1.0 to 3.0:1 and preferably 2.7:1 to 2.8:1; and from 20 wt % to 26wt % 4,4′-DDS as the curing agent.

Another preferred DEN/TRIF matrix resin includes from 19 wt % to 23 wt %triglycidyl-m-aminophenol (MY0600); from 14 wt % to 18 wt % hydrocarbonnovolac epoxy resin (TACTIX 556); from 7 wt % to 11 wt %polyethersulfone (5003P) as a toughening agent; from 9 wt % to 13 wt %polyamide 11 particles (Rislan PA11); from 18-22 wt % core shellparticles (MX-418); and from 21 wt % to 2.6 wt % 4,4′-DDS as the curingagent.

The prepreg may be molded using any of the standard techniques used toform composite parts. Typically, one or more layers of prepreg areplaced in a suitable mold and cured to form the final composite part.The prepreg of the invention may be fully or partially cured using anysuitable temperature, pressure, and time conditions known in the art,.Typically, the prepreg will be cured in an autoclave at temperatures ofbetween 160° C. and 190° C. The composite material may be cured using amethod selected from microwave radiation, electron beam, gammaradiation, or other suitable thermal or non-thermal radiation.

Composite parts made from the improved prepreg of the present inventionwill find application in making articles such as numerous primary andsecondary aerospace structures (wings, fuselages, bulkheads and thelike), but will also be useful in many other high performance compositeapplications including automotive, rail and marine applications wherehigh compressive strength, interlaminar fracture toughness andresistance to impact damage are needed.

Examples 1-7, which are examples of practice with respect to theDEN/TRIF/TETF matrix resin embodiment of the invention, are as follows:

EXAMPLE 1

A preferred exemplary resin formulation in accordance with the presentinvention is set forth in TABLE 1. A matrix resin was prepared b mixingthe epoxy ingredients at room temperature with the polyethersulfone toform a resin blend that was heated to 120° C. for 60 minutes tocompletely dissolve the polyethersulfone. The mixture was cooled to 80°C. and the rest of the ingredients added and mixed in thoroughly.

TABLE 1 Ingredient Amount (Wt %) Hydrocarbon epoxy novolac resin 10.0(TACTIX ®556) Trifunctional para-glycidyl amine (MY0510) 21.9N,N,N′,N′-tetraglycidyl-4,4′-diaminodiphenyl 18.2 methane (MY721)Thermoplastic Toughening Agent (polyether 11.5 sulfone - 5003P)Polyimide Particles (P84HCM) 3.0 Polyamide Particle (TR90) 9.0 Aromaticdiamine curing agent (3,3-DDS) 26.4

Exemplary prepreg was prepared by impregnating one or more layers ofunidirectional carbon fibers with the resin formulation of TABLE 1. Theunidirectional carbon fibers (12.K IM8 available from HexcelCorporation) were used to make a prepreg in which the matrix resinamounted to 35 weight percent of the total uncured prepreg weight andthe fiber areal weight was 192 grams per square meter (gsm). 26-plylaminates were prepared using standard prepreg fabrication procedures.The laminates were cured in an autoclave at 177° C. for about 2 hours.The cured laminates were tested to determine interlaminar fracturetoughness.

G2c is a standard test that provides a measure of the interlaminarfracture toughness of a cured laminate. G2c was determined as follows. A26-ply unidirectional laminate was cured with a 3 inch fluoroethylenepolymer (FEP) inserted along one edge, at the mid-plane of the layup,perpendicular to the fiber direction to act as a crack starter. Thelaminate was cured for 2 hours at 177° C. in an autoclave and gave anominal thickness of 3.8 mm. Consolidation was verified by C-scan. G2csamples were machined from the cured laminate. G2c was tested at roomtemperature in accordance with BSS7320. The G2c values listed below arethe average of the first and second cracks observed during the testingin accordance with BSS7320.

The G2c of the cured 26-ply laminate was 10.22. Open hole compression(OHT) and open hole compression (OHC) were also measured according tostandard procedures at room temperature and found to be above acceptablelimits for structural parts.

EXAMPLE 2

An exemplary prepreg having a DEN/TRIF/TETR resin matrix with theformula set forth in TABLE 2 was prepared in the same manner as Example1.

TABLE 2 Ingredient Amount (Wt %) Hydrocarbon epoxy novolac resin 14.10(TACTIX ®556) Trifunctional para-glycidyl amine (MY0510) 19.15N,N,N′,N′-tetraglycidyl-4,4′-diaminodiphenyl 17.85 methane (MY721)Thermoplastic Toughening Agent (polyether 11.50 sulfone - 5003P)Polyimide Particles (P84HCM) 3.0 Polyamide Particle (TR90) 9.0 Aromaticdiamine curing agent (3,3-DDS) 25.40

26-ply laminates were prepared, cured and tested for G2c at roomtemperature in the same manner as Example 1. The G2c was 13.16. The OHTand OHC were both also above acceptable limits for structural parts.

EXAMPLE 3

An exemplary prepreg was prepared in the same manner as Example 1,except that a DEN/TRIF/TETF resin formulation, as set forth in TABLE 3,was used as the prepreg resin matrix.

TABLE 3 Ingredient Amount (Wt %) Hydrocarbon epoxy novolac resin 17.0(TACTIX ®556) Trifunctional para-glycidyl amine (MY0510) 14.9N,N,N′,N′-tetraglycidyl-4,4′-diaminodiphenyl 18.2 methane (MY721)Thermoplastic Toughening Agent (polyether 11.5 sulfone - 5003P)Polyimide Particles (P84HCM) 6.0 Polyamide Particle (TR90) 6.0 Aromaticdiamine curing agent (3,3-DDS) 26.4

26-ply laminates were prepared, cured and tested for G2c at roomtemperature in the same manner as Example 1. The G2c was 10.47. The OHTand OHC were both also above acceptable limits for structural parts.

EXAMPLE 4

An exemplary prepreg was prepared in the same manner as Example 1,except that a DEN/TRIF/TETF matrix resin formulation, as set forth inTABLE 4, was used as the prepreg resin matrix.

TABLE 4 Ingredient Amount (Wt %) Hydrocarbon epoxy novolac resin 17.0(TACTIX ®556) Trifunctional meta-glycidyl amine (MY0610) 14.9N,N,N′,N′-tetraglycidyl-4,4′-diaminodiphenyl 18.2 methane (MY721)Thermoplastic Toughening Agent (polyether 11.5 sulfone - 5003P)Polyimide Particles (P84HCM) 6.0 Polyamide Particle (TR90) 6.0 Aromaticdiamine curing agent (3,3-DDS) 26.4

26-ply laminates were prepared, cured and tested for G2c at roomtemperature in the same manner as Example 1. The G2c was 9.15. The OHTand OHC were both also above acceptable limits for structural parts.

EXAMPLE 5

An exemplary prepreg was prepared in the same manner as Example 1,except that a resin formulation in accordance with the presentinvention, as set forth in TABLE 5, was used as the prepreg resinmatrix.

TABLE 5 Ingredient Amount (Wt %) Hydrocarbon epoxy novolac resin 10.0(TACTIX ®556) Trifunctional para-glycidyl amine (MY0510) 21.9N,N,N′,N′-tetraglycidyl-4,4′-diaminodiphenyl 18.2 methane (MY721)Thermoplastic Toughening Agent (polyether 11.5 sulfone - 5003P)Polyimide Particles (P84HCM) 6.0 Polyamide Particle (TR90) 6.0 Aromaticdiamine curing agent (3,3-DDS) 26.4

26-ply laminates were prepared, cured and tested for G2c at roomtemperature in the same manner as Example 1. The G2c was 9.50. The OHTand OHC were both also above acceptable limits for structural parts.

EXAMPLE 6

An exemplary prepreg was prepared in the same manner as Example 1,except that a resin formulation in accordance with the presentinvention, as set forth in TABLE 6, was used as the prepreg resinmatrix.

TABLE 6 Ingredient Amount (Wt %) Hydrocarbon epoxy novolac resin 14.75(TACTIX ®556) Trifunctional para-glycidyl amine (MY0510) 20.03N,N,N′,N′-tetraglycidyl-4,4′-diaminodiphenyl 18.67 methane (MY721)Thermoplastic Toughening Agent (polyether 8.0 sulfone - 5003P) PolyimideParticles (P84HCM) 3.0 Polyamide Particle (TR90) 9.0 Aromatic diaminecuring agent (3,3-DDS) 26.56

26-ply laminates were prepared, cured and tested for G2c at roomtemperature in the same manner as Example 1. The G2c was 9.31. The OHTand OHC were both also above acceptable limits for structural parts.

EXAMPLE 7

An exemplary prepreg was prepared in the same manner as Example 1,except that a resin formulation in accordance with the presentinvention, as set forth in TABLE 7, was used as the prepreg resinmatrix.

TABLE 7 Ingredient Amount (Wt %) Hydrocarbon epoxy novolac resin 10.0(TACTIX ®556) Trifunctional para-glycidyl amine (MY0510) 22.0N,N,N′,N′-tetraglycidyl-4,4′-diaminodiphenyl 20.5 methane (MY721)Thermoplastic Toughening Agent (polyether 8.0 sulfone - 5003P) PolyimideParticles (P84HCM) 3.0 Polyamide Particle (TR90) 9.0 Aromatic diaminecuring agent (3,3-DDS) 27.5

26-ply laminates were prepared, cured and tested for G2c at roomtemperature in the same manner as Example 1. The G2c was 7.30. The OHTand OHC were both also above acceptable limits for structural parts.

COMPARATIVE EXAMPLES 1-7

Comparative prepregs and laminates with respect to the DEN/TRIF/TETFmatrix resin embodiment were prepared, cured and tested in the samemanner as Example 1, except that the resin formulations were as setforth in TABLE 8. The amounts listed in TABLE 8 are weight percent ofthe total resin mixture. 26-ply laminates were prepared, cured andtested for G2c at room temperature in the same manner as Example 1. TheG2c results are listed in the table.

TABLE 8 Ingredient C1 C2 C3 C4 C5 C6 C7 TACTIX ®556 10.0 10.0 14.1 10.05.00 14.75 5.00 MY0510 21.9 21.9 19.16 22.00 24.08 20.03 24.08 MY72118.2 18.2 17.89 20.50 22.44 18.67 22.44 5003P 11.5 11.5 11.5 8.0 8.0 8.08.0 P84HCM 12.0 0 9.0 0 3.0 0 0 TR90 0 12.0 3.0 12.0 9.0 12.0 12.03,3-DDS 26.4 26.4 25.4 27.51 28.49 26.56 28.49 G2c 4.68 9.97 7.12 5.314.29 8.36 2.64

The viscosity of the resin formulation should he such that the prepregresin formulation can he suitably impregnated or otherwise applied tothe fibrous reinforcement using accepted prepreg formation processes.The viscosity profile of the resin provides a guide as to thesuitability of a resin formulation for use as a prepreg resin. Theviscosity profile is determined by raising the temperature of the resinfrom room temperature at a rate of 2° C. per minute and monitoring theviscosity of the resin. As the resin is heated, the viscosity typicallydecreases to a minimum and then increases as polymerization progresses.The minimum viscosity of the resin and the temperature at which thisminimum viscosity is reached provides an indication of the suitabilityof the resin for a given prepreg process. When the term “minimumviscosity” is used herein, it means the minimum viscosity that ismeasured during determination of the viscosity profile for the resin.

In many prepreg manufacturing processes, it is desirable that theminimum viscosity be such that adequate resin flow occurs duringformation of the prepreg to ensure complete impregnation of the fiberreinforcement. The desired minimum viscosity for the prepreg resin insuch processes depends upon a number of factors including the desireddegree of impregnation, impregnation temperature and pressure, themethod used to accomplish impregnation and the type of fibrousreinforcement.

The preferred minimum viscosity of the prepreg resin is in the range offrom 55 to 75 Poise (P) for those prepreg processes that require arelatively high viscosity prepreg resin. For prepreg processes thatrequire a relatively low viscosity prepreg resin, the preferred minimumviscosity of the prepreg resin is in the range of from 25 to 45 P. Itwas found that amounts of PES in the range of 10-13 weight percentprovides prepreg resins in accordance with the present invention thatare in the higher minimum viscosity range. PES amounts in the range of7-9 weight percent provide prepreg resins in accordance with the presentinvention that are in the lower minimum viscosity range.

The viscosity profiles were determined for Examples 1-7 and ComparativeExamples 1-7. The minimum viscosity and temperature at which the minimumviscosity was reached is set forth in TABLE 9. The amount of PES andTACTIX 556 resin in the formulation along with the G2c values are alsotabulated in the table.

TABLE 9 Minimum Temperature at Viscosity Minimum Poise Viscosity PESTACTIX (P) (° C.) G2c WT % 556 Example 1 61.34 137.0 10.22 11.5 10.0Example 2 66.60 130.8 13.16 11.5 14.1 Example 3 64.8 136.4 10.47 11.517.0 Example 4 70.6 136.2 9.15 11.5 17.0 Example 5 56.3 134.5 9.50 11.510.0 Example 6 34.4 124.0 9.31 8.0 14.75 Example 7 32.55 124.1 7.30 8.010.0 Comp. Ex. 1 — — 4.68 11.5 10.0 Comp. Ex. 2 85.5 130.7 9.97 11.510.0 Comp. Ex. 3 55.9 136.4 7.12 11.5 14.1 Comp. Ex. 4 41.23 118.9 5.138.0 10.0 Comp. Ex. 5 30.1 122.3 4.29 8.0 5.0 Comp. Ex. 6 57.1 116.3 8.368.0 14.75 Comp. Ex. 7 47.8 116.1 2.64 8.0 5.0

Examples 1-5 are exemplary of DEN/TRIF/TETF resins that have a minimumviscosity which falls within the above mentioned high viscosity range.The DEN/TRIF/TETF resin formulation of Example 1 is preferred because itprovides an unexpectedly high G2c of over 10 when using only 10.0 weightpercent TACTIX 556 resin in combination with 9.0 weight percent TR90polyamide particles and 3.0 weight percent P84 polyimide particles.Examples 3 and 4, which use 17.0 weight percent. TACTIX 556 resin incombination with 6.0 weight percent. TR90 polyamide particles and 6.0weight percent P84 polyimide particles, also unexpectedly achieve ratherhigh G2c values while keeping the minimum viscosity within the desiredhigh viscosity range.

The DEN/TRIF/TETF resin formulation of Example 2. is particularlypreferred because it provides an increase of G2c up to 13.16 when 14.10weight percent TACTIX 556 resin is used in combination with 9.0 weightpercent TR90 polyamide particles and 3.0 weight percent P84 polyimideparticles. Such a high G2c value (13.16) is particularly unexpected.

The high values for G2c that are obtained when TACTIX 556 resin iscombined with TR90 polyamide particles and P84 polyimide particles, asset forth above, is unexpected because Comparative Example 1 shows thatthe use of P84 polyamide particles alone (C1) provides a relatively lowG2c of only 4.68. Comparative Example 2 shows that the use of TR90polyamide particles alone (C2) provides a much higher G2c of 9.97. It isunexpected that combinations of P84 polyimide particles and TR90polyamide particles are capable of providing higher G2c values than canbe achieved using either type of particle alone.

In view of Comparative Examples 1 and 2, Comparative Example 3 shows anexpected decrease in G2c (7.12) when 9.0 weight percent P84 polyimideparticles are combined with 3.0 weight percent TR90 polyamide particles.In view of Comparative Examples 1-3, it is unexpected that adding anyamount of P84 polyimide particles to a thermoplastic particle componentmade up of TR90 polyamide particles would synergistically increase theG2c values to at least 10 as shown in Examples 1-3. It is particularlyunexpected that a G2c of 13.6 could be achieved when the amount ofTACTIX 556 resin is increased from 10.0 to 14.1 weight percent as shownin Examples 1 and 2.

The high G2c values that are obtained with the DEN/TRIF/TETF matrixresin formulations according to Examples 1-5 is accomplished whilekeeping the minimum viscosity of the resins at between 25 and 75 Poise.As shown in Comparative Example 2, the use of TR90 polyamide particlesalone does provide a relatively high G2c of 9.97. However, the minimumviscosity is 85.5 Poise, which is above the desired high viscosity rangeof 55-75 Poise.

Examples 6-7 are exemplary of DEN/TRIF/TETF resins that have a minimumviscosity which falls within the above mentioned low viscosity range.The lower viscosity levels provided by using lower amounts (7-9 wt %) ofPES (See Example 6-7 and Comparative Examples 4-7) also results in adecrease in the G2c levels of the cured laminates. Even so, the resinformulation of Example 6-7 provide an unexpectedly high G2c. Acomparison of Example 6 to Comparative Example 6 (14.75 wt % TACTIX 556resin) shows that the (32,c is synergistically increased from 8.36 to9.31 when the thermoplastic particle component is changed from 12.0 wt %TR90 polyamide particles to a mixture of 9.0 wt % TR90 polyamideparticles and 3.0 wt % P84 polyimide particles. In addition, acomparison of Example 7 to Comparative Example 4 (10.0 wt % TACTIX 555resin) shows that the G2c is synergistically increased from 5.13 to 7.30when the thermoplastic particle component is changed from 12.0 wt % TR90polyamide particles to a mixture of 9.0 wt % TR90 polyamide particlesand 3.0 wt % P84 polyimide particles.

The observed synergistic effect provided by the addition of polyimideparticles to TR90 polyamide particles in a DEN/TRIF/TETF matrix resin isnot expected to occur unless the thermoplastic particle componentcontains at least 15 weight percent polyimide particles, based on thetotal weight of the thermoplastic component, with the remainder of thethermoplastic particle component being TR90 polyamide particles. Thesynergistic effect is expected to end when the thermoplastic particlecomponent contains more than 70 weight percent polyimide particles,based on the total weight of the thermoplastic component, with theremainder of the thermoplastic particle component being TR90 polyamideparticles. The maximum synergistic effect is provided when thethermoplastic particle component contains from 20 to 30 weight percentpolyimide particles, based on the total weight of the thermoplasticcomponent, with the remainder of the thermoplastic particle componentbeing TR90 polyamide particles.

The inclusion of TACTIX 556 resin in the epoxy resin component of aDEN/TRIF/TETF matrix resin provides a substantial increase in the G2cfracture resistance. Examples 6 and 7 show that the G2c goes from 9.31to 7.30 when the amount of TACTIX 556 resin is reduced from 14.75 to10.0 weight percent. Comparative Example 5 shows that the G2c drops downto a low value 4.29 when the amount of TACTIX 556 resin is reduced to5.0 weight percent. Comparative Examples 4 and 6-7 show that a similardrop in G2c occurs when the amount of TACTIX 556 resin is reduced incomparative resins that contain only TR90 polyamide particles as thethermoplastic particle component. Accordingly it is preferred that theamount of hydrocarbon epoxy novolac resin present in the DEN/TRI/TETFmatrix resin formulations of the present invention be at least 8 weightpercent, based on the total weight of the resin.

Examples 8-23, which are examples of practice with respect to theDEN/TRIF matrix resin embodiment of the invention, are as follows:

EXAMPLE 8

An exemplary DEN/TRIF resin formulation in accordance with the presentinvention is set forth a TABLE. 10. An uncured matrix resin was preparedby mixing, the epoxy ingredients at room temperature with thepolyethersulfone to form a resin blend that was heated to 120° C. for 60minutes to completely dissolve the polyethersulfone. The mixture wascooled to 80° C. and the rest of the ingredients were added and mixed inthoroughly in the same manner as Examples 1-7.

TABLE 10 Ingredient Amount (Wt %) dicyclopentadiene novolac epoxy resin21.92 (TACTIX 556) Trifunctional meta-glycidyl amine (MY0600) 31Thermoplastic Toughening Agent (polyether 9.0 sulfone - 5003P)Crosslinked PA12 Particles (ORGASOL 2009) 4.00 Non-crosslinked - PA11Particles (Rislan 11) 11.00 Aromatic diamine curing agent (4,4′-DDS)23.09

Exemplary prepreg was prepared by impregnating a layer of unidirectionalcarbon fibers with the resin formulation of TABLE 10 to form a prepregcomposed of reinforcing fibers and an uncured resin matrix. Theunidirectional carbon fibers were 12K IM7. The uncured resin matrixamounted to 35 weight percent of the total uncured prepreg weight andthe fiber areal weight of the uncured prepreg was 145 grams per squaremeter (gsm).

The prepreg was used to form a laminate in the same manner as Examples1-7. The laminate was cured in an autoclave at 177° C. for about 2 hoursto form a cured test laminate. The cured test laminate was divided intotest samples that were examined to determine open hole compressivestrength (OHC) and open hole tensile strength (OHT).

The OHC and OHT test samples were examined under dry conditions(relative humidity of 10% to 50%) at room temperature (21 to 24° C.).OHC was tested in accordance with D6-83079-71 Type II Class 1. OHT wastested in accordance with D6-83079-62 Type I Class 1.

Cured test samples were also subjected to standard tests to determinetheir tolerance to damage (CAI). Compression after Impact (CAI) wasdetermined using a 270 in-lb impact against a 32-ply quasi-isotropiclaminate. The specimens were machined, impacted and tested in accordancewith Boeing test method BSS7260 per BMS 8-276. Values are normalized toa nominal cured laminate thickness of 0.18 inch.

The cured test samples were also subjected to testing in accordance withASTM D5528 in the same manner as Examples 1-7 in order to determine G1cand G2c.

When the terns “OHT”, “OHC”, “CAI”, “G1c” and G2c” are used herein todefine a property exhibited by a cured laminate, the terms mean theproperty as measured by the above described testing procedures.

Additional exemplary DEN/TRIF matrix resin formulations (Examples 9-23)are set forth in TABLES 11-13. The exemplary DEN/TRIF matrix resinformulations were used to make prepreg that was cured and tested in thesame manner as Examples 1-8, except that Examples 22 and 23 used 12K IM8carbon fibers rather than 12K 1M7 fibers. The results of OHT, OHC, CAI,G1c and G2c testing with respect to Examples 8-23, which were conductedas described above, are set forth in TABLES 11-13.

TABLE 11 Ingredient Ex 8 Ex 9 Ex 10 Ex 11 Ex 12 Ex 13 TACTIX ®556 21.9222.51 21.92 21.92 21.92 22.95 MY0610 31 31.8 31 31 31 32.46 PES (5003P)9.00 7.00 9.00 9.00 9.00 9.42 RISLAN 11 11.00 11.00 11.00 12.00 13.0011.00 ORGASOL 2009 4.00 4.00 4.00 3.00 2.00 0 3,3′-DDS 0 0 23.09 0 0 04,4′-DDS 23.09 23.69 0 23.09 23.09 24.17 OHT 166.1 160.2 153.0 — — 156.7OHC 80.1 78.56 80.3 — — — CAI 54.4 53.68 53.2 — — 51.17 G1c 3.61 3.373.52 3.57 3.68 3.03 G2c 15.70 14.93 15.38 15.55 15.67 12.55

TABLE 12 Ingredient Ex 14 Ex 15 Ex 16 Ex 17 Ex 18 Ex 19 TACTIX ®55622.69 22.43 22.18 21.92 14.87 21.92 MY0610 32.09 31.73 31.36 31 38.31 31PES (5003P) 9.32 9.21 9.11 9.00 9.32 9.00 RISLAN 11 12.00 13.00 14.0015.00 0 0 ORGASOL 0 0 0 0 0 0 2009 Polyamide 0 0 0 0 12.00 0 TR90Polyamide 0 0 0 0 0 15.00 CX7323 4,4′-DDS 23.90 23.63 23.36 23.09 25.523.09 OHT 158.8 161.6 159.6 160.1 140.7 163.2 OHC — — — — — — CAI 51.152.74 53.19 55.22 — 50.06 G1c 3.09 3.11 3.10 3.29 3.12 4.12 G2c 15.7214.09 17.93 14.70 13.69 13.11

TABLE 13 Ingredient Ex 20 Ex 21 Ex 22 Ex 23 C8 C9 TACTIX ®556 15.56 021.92 14.37 14.71 14.00 XD-1000-2L 0 23.01 0 0 0 0 MY0610 21.05 30.3331.00 37.00 0 0 MY0510 0 0 0 0 37.00 0 MY721 0 0 0 0 0 30.00 Bis A Epoxy0 0 0 0 0 4.53 Bis F Epoxy 0 0 0 0 0 5.67 PES (5003P) 9.00 9.00 9.009.00 9.00 9.00 RISLAN 11 11.00 15.00 11.00 11.00 6.00 11.00 ORGASOL 0 04.00 4.00 6.00 6.00 2009 Core-shell 20.00 0 0 0 0 0 MX-418 PSG particles0 0 0 0 3.00 0 4,4′-DDS 23.39 22.66 23.09 24.63 24.29 21.80 OHT 170.2160.4 166.9 151 135 145.8 OHC — — 73.42 70.77 75.79 67.82 CAI — 55.2953.01 — — — G1c 3.16 3.41 3.54 — — — G2c 12.84 15.52 13.22 — — —

The matrix resins formulations for Examples 8-23, as set for the inTABLES 11-13 are exemplary of suitable DEN/TRIF matrix resins inaccordance with the present invention. Many other possible similar forare possible in accordance with the present invention provided that thecured laminate made using the DEN/TRIF resin formulation exhibits thefollowing properties: 1) OHT of at least 140, preferably at least 150and most preferably at least 160; 2) OHC of at least 70, preferably atleast 75 and most preferably at least 80; 3) CAI of at least 45,preferably at least 50 and most preferably at least 55; 4) G1c of atleast 3.0, preferably at least 3.2 and most preferably at least 3.5; and3) G2c of at least 12.0, preferably at least 14.0 and most preferred atleast 15.0.

DEN/TRIF matrix resin formulations which correspond to Example 8 arepreferred resin formulations because they provide very high fracturetolerance (G1c and G2c) while unexpectedly maintaining relatively highCAI, OHT and OHC.

DEN/TRIF matrix resin formulations which correspond to Example 20 arealso preferred resin formulations because the inclusion of core shellparticles in a DEN/TRIF-type formulation was found to provide high OHTand acceptable fracture tolerance, as measured by G2c. In addition, ofall of the DEN/TRIF examples tested, the R-curve fracture toughness ofExample 20, as measured by crack growth resistance (R-curve) analysis,was unexpectedly better than the others. R-curve analysis is a knowntype of test procedure that is commonly used for investigating thefracture mechanics of laminates and other materials. ASTM Standard E561is an example of a commonly used R-curve analysis procedure with manyvariations of this procedure commonly in use. The laminates made usingDEN/TRIF exemplary formulations were tested using an R-curve testingprocedure that is similar to ASTM E561. Example 20 was the only laminatethat had a rising R-curve. A rising R-curve, as opposed to a negative orflat R-curve, is considered indicative of a high level of crack growthresistance and fracture toughness.

The DEN/TRIF matrix resin formulations are combined with an intermediatemodulus carbon fiber, such as IM7 or IM8 , to form prepreg that can beused to form uncured laminates that are curable to form cured laminatesthat have properties which fall within the above ranges. To verify thateach DEN/TRIF exemplary matrix resin meets the requirements of thepresent invention, it is necessary to test each laminate to confirm thatit meets or exceeds the OHT, OHC, CAI, G1c and G2c limits, as set forthabove.

Comparative Example 8 (see TABLE 13) involves the use of MY0510 in placeof MY0610 in the resin component of a DEN/TRIF matrix resin. ComparativeExample 8 was prepared and tested in the same manner as Examples 22-23.The OHT for Comparative Example 8 was 135. This is below the thresholdOHT of 140 which is required for the matrix resin to be acceptable inaccordance with the present invention. A small amount of PSG particlesare present in the matrix resin of Comparative Example 8. PSG particlesare not present in Examples 22-23. The inclusion of a small amount ofPSG particles is expected to have a. relatively small effect on OHT. Itis believed that the relatively low OHT for Comparative Example 8 is atleast partly due to the use of MY0510 in place of MY0610. Accordingly,it is preferred that triglycidyl-meta-aminophenol (MY610) resin, ratherthan triglycidyl-para-aminophenol (MY0510) resin, be used in DEN/TRIFmatrix resin embodiments.

The negative effect of using MY0510 instead of MY0610 in the DEN/TRIFmatrix resin embodiments is contrary to the positive effect that isobserved when MY0510 is used instead of MY0610 in the DEN/TRIF/TETFmatrix resin embodiments. As shown by a comparison of Example 3 withExample 4, the G2c dropped from 10.47 to 9.15 when MY0610 was used inplace of MY0510 in a DEN/TRIF/TETF matrix resin. Accordingly, it ispreferred that triglycidyl-para-aminophenol (MY0510) resin, rather thantriglycidyl-metal-aminophenol (MY0610) resin, be used in DEN/TRIF/TETFmatrix resin embodiments.

Comparative Example 9 (see TABLE 13) involves the use of approximately10 wt % difunctional epoxy resins (Bisphenol A and Bisphenol F epoxyresins) in combination with TACTIX®556 and MY721 in the epoxy resincomponent. The resulting OHC was 67.82, which is below the threshold of70 for laminates made using DEN/TRIF matrix resin formulations.Accordingly, the inclusion of difunctional epoxy resins in either matrixresin embodiment should be kept below 5 wt % and preferably below 1 wt%, as discussed above.

Having thus described exemplary embodiments of the present invention, itshould be noted by those skilled in the art that the within disclosuresare exemplary only and that various other alternatives, adaptations andmodifications may be made within the scope of the present invention.Accordingly, the present invention is not limited by the above-describedembodiments, but is only limited by the following claims.

What is claimed is:
 1. A pre-impregnated composite material comprising:A) reinforcing fibers comprising carbon fibers; and B) an uncured resinmatrix comprising: a) an epoxy resin component comprising from 17 to 27weight percent of a hydrocarbon epoxy novolac resin, based on the totalweight of said uncured resin matrix, and from 26 to 36 weight percent ofa triglycidyl meta-aminophenol, based on the total weight of saiduncured resin matrix; b) 11 to 19 weight percent of a thermoplasticparticle component based on the total weight of said uncured resinmatrix, said thermoplastic particle component comprises a mixture of afirst group of polyamide particles that do not comprise crosslinkedpolyamide and a second group of polyamide particles that comprisecrosslinked polyamide; c) 7 to 12 weight percent of a thermoplastictoughening agent, based on the total weight of said uncured resinmatrix, said thermoplastic toughening agent comprising polyethersulfone;and d) 17 to 27 weight percent of a curing agent, based on the totalweight of said uncured resin matrix, said curing agent comprising4,4′-diaminodiphenyl sulphone and/or 3,3′-diaminodiphenyl sulphone. 2.The pre-impregnated composite material according to claim 1 wherein theweight ratio of said first group of polyamide particles to said secondgroup of polyamide particles is from 4:1 to 1.5:1.
 3. Thepre-impregnated composite material according to claim 2 wherein theweight ratio of said first group of polyamide particles to said secondgroup of polyamide particles is from 3.5:1 to 2.5:1.
 4. Thepre-impregnated composite material according to claim 1 wherein saidfirst group of polyamide particles comprises polyamide 11 particles andsaid second group of particles comprises crosslinked polyamide 12particles that comprise crosslinked polyamide
 12. 5. The pre-impregnatedcomposite material according to claim 4 wherein the weight ratio of saidpolyamide 11 particles to said crosslinked polyamide 12 particles isfrom 4:1 to 1.5:1.
 6. The pre-impregnated composite material accordingto claim 5 wherein the weight ratio of said polyamide 11 particles tosaid crosslinked polyamide 12 particles is from 3.5:1 to 2.5:1.
 7. Thepre-impregnated composite material according to claim 4 wherein saidcuring agent comprises 4,4′-diaminodiphenyl sulphone.
 8. Thepre-impregnated composite material according to claim 1 wherein saidreinforcing fibers comprise a plurality of carbon fiber tows which eachcomprises from 10,000 to 14,000 carbon filaments wherein the weight perlength of each of said carbon tows is from 0.2 to 0.6 grams per meterand wherein the tensile strength of each of said carbon tows is from 750to 860 kilopounds per square inch and the tensile modulus of each ofsaid carbon tows is from 35 to 45 megapounds per square inch.
 9. Thepre-impregnated composite material according to claim 1 wherein saidcuring agent comprises 4,4′-diaminodiphenyl sulphone.
 10. A compositepart or structure that has been formed by curing a pre-impregnatedcomposite material according to claim
 1. 11. The composite part orstructure according to claim 10 wherein said composite part or structureforms at least part of an aircraft primary structure.
 12. A method formaking a composite part or structure comprising the step of providing apre-impregnated composite material according to claim 1 and curing saidpre-impregnated composite material to form said composite part orstructure.
 13. The method for making a composite part or structureaccording to claim 12 wherein said composite part or structure forms atleast part of an aircraft primary structure.
 14. A method for making acomposite part or structure according to claim 12 wherein said firstgroup of polyamide particles comprises polyamide 11 particles and saidsecond group of particles comprises crosslinked polyamide 12 particlesthat comprise crosslinked polyamide
 12. 15. A method for making acomposite part or structure according to claim 12 wherein said curingagent comprises 4,4′-diaminodiphenyl sulphone.
 16. A method for making acomposite part or structure according to claim 12 wherein saidreinforcing fibers comprise a plurality of carbon fiber tow which eachcomprises from 10,000 to 14,000 carbon filaments wherein the weight perlength of each of said carbon tows is from 0.2 to 0.6 grams per meterand wherein the tensile strength of each of said carbon tows is from 750to 860 kilopounds per square inch and the tensile modulus of each ofsaid carbon tows is from 35 to 45 megapounds per square inch.
 17. Amethod for making a pre-impregnated composite material that is curableto form a composite part, said method comprising the steps of: A)providing reinforcing fibers comprising carbon fibers; and B)impregnating said reinforcing fibers with an uncured resin matrixwherein said uncured resin matrix comprises: a) an epoxy resin componentcomprising from 17 to 27 weight percent of a hydrocarbon epoxy novolacresin, based on the total weight of said uncured resin matrix, and from26 to 36 weight percent of a triglycidyl meta-aminophenol, based on thetotal weight of said uncured resin matrix; b) 11 to 19 weight percent ofa thermoplastic particle component based on the total weight of saiduncured resin matrix, said thermoplastic particle component comprises amixture of a first group of polyamide particles that do not comprisecrosslinked polyamide and a second group of polyamide particles thatcomprise crosslinked polyamide; c) 7 to 12 weight percent of athermoplastic toughening agent, based on the total weight of saiduncured resin matrix, said thermoplastic toughening agent comprisingpolyethersulfone; and d) 17 to 27 weight percent of a curing agent,based on the total weight of said uncured resin matrix, said curingagent comprising 4,4′-diaminodiphenyl sulphone and/or3,3′-diaminodiphenyl sulphone.
 18. The method for making apre-impregnated composite material according to claim 17 wherein saidfirst group of polyamide particles comprises polyamide 11 particles andsaid second group of particles comprises crosslinked polyamide 12particles that comprise crosslinked polyamide
 12. 19. The method formaking a pre-impregnated composite material that is curable to form acomposite part according to claim 17 wherein said curing agent comprises4,4′-diaminodiphenyl sulphone.
 20. The method for making apre-impregnated composite material that is curable to form a compositepart according to claim 17 wherein said reinforcing fibers comprise aplurality of carbon fiber tow which each comprises from 10,000 to 14,000carbon filaments wherein the weight per length of each of said carbontows is from 0.2 to 0.6 grams per meter and wherein the tensile strengthof each of said carbon tows is from 750 to 860 kilopounds per squareinch and the tensile modulus of each of said carbon tows is from 35 to45 megapounds per square inch.